CN106086652A - High strength heat resistant the cold heading steel and production method thereof - Google Patents
High strength heat resistant the cold heading steel and production method thereof Download PDFInfo
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- CN106086652A CN106086652A CN201610632572.0A CN201610632572A CN106086652A CN 106086652 A CN106086652 A CN 106086652A CN 201610632572 A CN201610632572 A CN 201610632572A CN 106086652 A CN106086652 A CN 106086652A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- Physics & Mathematics (AREA)
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a kind of high strength heat resistant the cold heading steel and production method thereof, its composition is by weight percentage: C 0.38%～0.50%, Si 0.30%～0.40%, Mn 0.75%～1.00%, P≤0.015%, S≤0.015%, Cr 0.90%～1.20%, Mo 0.35%～0.45%, V 0.25%～0.35%, [O]≤15ppm, [N]≤45ppm, surplus is Fe and trace impurity.This wire rod uses Cr V Mo microalloying, it is ensured that Elements Diffusion is uniform, and Control of gas content is excellent, makes wire rod have good heat resistance；This wire rod possesses good intensity and heat resistance, and does not add precious metal, and cost is relatively low.This method is without increasing equipment and investment, do not increase production cost, make full use of existing equipment and technique, the requirement of the heat-resistant stable according to downstream manufacturing enterprise, the high-strength bolt that gained wire rod is made is on active service under 600 DEG C of conditions of high temperature, good intensity and toughness index can be kept, there is good heat-resistant stable, intensity and heat resistance.
Description
Technical field
The present invention relates to a kind of wire rod and production method thereof, especially a kind of high strength heat resistant the cold heading steel and production thereof
Method.
Background technology
Turbine making industry is the basis of power industry, embodies a national machine-building level.China's steam turbine
Yield accounts for the 1/4 of the world, and market is huge.Steam turbine high-temperature parts must select the heat proof material using temperature the highest, the highest
The strong material manufacture of heat that cylinder pressure and stop valve bolt etc. must use high-temperature behavior excellent.Recent domestic all attaches great importance to height
The development of temperature bolt technology, American-European, Japan and other countries has been walked in prostatitis.
Turbine bolt works under the conditions of high temperature, heavily stressed, aggressive atmosphere, and it must have good creep with material
Enduring quality and good antioxygenic property.High temperature bolt at room temperature assembles and fastens, after being passed through high temperature and high pressure steam
Cylinder and bolt all can expanded by heating.The universal thermal coefficient of expansion of components of steam turbine steel fastened is relatively low, therefore coordinate with it
The thermal coefficient of expansion of high temperature bolt material also should be relatively low, the pretightning force that such guarantee is enough.High temperature bolt should have higher
Stress relaxation resistance, it is ensured that cylinder will not leak gas.High strength heat resistant the cold heading steel agrees with above-mentioned turbine bolt requirement, with
Other kinds of turbine bolt steel is compared, and comprehensive mechanical property is more stable, saves alloying element, tallies with the national condition,
Cost performance is higher.
Owing to heat-resistant stable requires relatively strict, major part dependence on import, the most domestic about heat-resistant stable
High intensity steel wire rod and production method thereof are less.Chinese patent CN200580016043.8 discloses a kind of resistance to high temperature corrosion
Rustless steel, it belongs to rustless steel field, is only applicable to SOFC connector material.Chinese patent application
200810200104.1 disclose a kind of heat-resistance structural steel, its manufacture method and application, obtain pearlite+ferrum by controlled rolling and controlled cooling
Ferritic tissue, has good elevated temperature strength；But organizational controls lacks universality, and produces through electric furnace, relatively costly, and
The important indicator resistance for delayed fracture of heat resisting steel is not accounted for, poor to Control of gas content, field trash and fatigue life
There is greater risk.Chinese patent application 201310282347.5 discloses a kind of low-alloy multielement high-strength heat-resistant steel and
Manufacture method, it is to add Ni and special modulation process by high Mn, adds cost and production cycle, and low strength.
Mostly prior art is, by adding precious metal and strengthening the means of downstream Technology for Heating Processing, to improve the resistance to of product
High-temperature behavior；And process costs is higher, lack technique universality dissemination.
Summary of the invention
The technical problem to be solved in the present invention is to provide that a kind of performance is good, the high strength heat resistant the cold heading steel of low cost；
Present invention also offers the production method of a kind of high strength heat resistant the cold heading steel.
For solving above-mentioned technical problem, the technical solution used in the present invention is: composition is by weight percentage: C
0.38%～0.50%, Si 0.30%～0.40%, Mn 0.75%～1.00%, P≤0.015%, S≤0.015%, Cr 0.90%～
1.20%, Mo 0.35%～0.45%, V 0.25%～0.35%, [O]≤15ppm, [N]≤45ppm, surplus is Fe and trace is miscellaneous
Matter.
The metallographic structure of wire rod of the present invention is mainly made up of bainite.
Wire rod specification of the present invention is Φ 5.5～38mm.
The inventive method includes steel-making, cogging, rolling and refrigerating work procedure；Described steel making working procedure includes converter smelting, LF stove
Refine, RH stove vacuum outgas and casting process, the percentage by weight of gained continuous casting billet composition is described above.
Steel making working procedure described in the inventive method: the inlet temperature of LF stove refine is 1490～1510 DEG C；RH stove vacuum outgas
Inlet temperature be 1680～1700 DEG C.Described steel making working procedure: the pulling rate of casting process is 0.6～0.9m/min.
Cogging operation described in the inventive method: continuous casting billet is heated to 1150～1250 DEG C and carries out cogging.
Rolling process described in the inventive method: be heated to 1150～1200 DEG C and roll, laying temperature is 750～850
℃。
Refrigerating work procedure described in the inventive method: control cooldown rate, at 1.5～2.0 DEG C/s, is cooled to 600 DEG C of time controls refrigeration
But speed is at 0.5 DEG C/s and following.
Present component design principle is as follows:
Carbon: be the essential element improving hardness of steel, it is ensured that the phosphorus content that certain intensity must be certain.Carbon can also expand and surely
Determine austenite, thus improve the elevated temperature strength of heat resisting steel.Control 0.38～0.50% carbon content can ensure that obtain enough strong
Degree, makes steel have good thermostability simultaneously.
Chromium, silicon: the element that these ferrites are formed, at high temperature can promote metal surface to generate fine and close oxide-film, anti-
Only continue oxidation, be non-oxidizability and the essential element of high temperature resistance gas attack improving steel.But the too high meeting of silicone content makes room temperature
Plasticity and thermoplasticity severe exacerbation.Chromium can significantly improve the recrystallization temperature of low-alloy steel, adds 1% in Mayari
Left and right chromium just can improve the creep-resistant property of steel, the particularly Mayari containing 1%Cr and 0.4%Mo significantly and can substantially carry
Its heat resistance high.When chromium content of the present invention is 0.90～1.20%, strengthening effect is preferable.Control Si content 0.30～0.40% can obtain
Obtain excellent thermostability and obdurability.
Manganese: can be formed and stable austenite.Nickel can improve the elevated temperature strength of austenitic steel and improve anti-carburizing.Though manganese
So can form austenite for nickel, but compromise the oxidisability of heat resisting steel.In view of the high price of nickel element, controlling Mn content is
0.75～1.00%.
Molybdenum: relative to other alloying elements, molybdenum atom is the biggest.It is very effective hardening agent, can improve the creep of steel
Intensity to can about 600 DEG C use degree.Molybdenum atom volume is big prevents the migration to crystal boundary of the arsenic atom effectively,
Thus prevent temper brittleness.Molybdenum can also reduce the activity of hydrogen in steel, is substantially reduced the suction hydrogen tendency of steel；And can hinder consumingly
The forming core of carbide and growing up, reduces the hydrogen storage trap in steel；Also hydrogen can be stoped to spread and make the degree of hydrogen induced cracking (HIC) drop simultaneously
Low to minimum.In the present invention add 0.35～0.45% molybdenum be most economical effective content.
Sulfur: sulfur is the harmful element in steel, S can only be dissolved in the molten steel of high temperature, is little to dissolve in solid iron, with
Grain boundaries in solid steel presented in FeS field trash, easily causes cracking during hot-working, the most hot-short.For ensureing one
Fixed cold heading performance and cutting ability, hot-working character, its content should be strict controlled in 0.015% and less.
Phosphorus: phosphorus has solution strengthening effect, can improve intensity and the hardness of steel, but can drastically reduce the impact flexibility of steel, phosphorus
Can gather at grain boundaries, form serious segregation, cause temper brittleness, its content is strict controlled in≤level of 0.015%.
Vanadium: vanadium can form carbon vanadium compounds disperse educt minutely, thus improves the creep strength of material, i.e. to improving steel
Heat resistance have preferably effect.Why vanadium can improve its heat resistance in steel is all the carbon by forming fine uniform distribution
Compound and work, because the carbide of vanadium is a kind of sufficiently stable carbide.Add again additionally, vanadium also has prevention steel billet
The effect of the recrystallization temperature of Austenite Grain Growth, raising steel during heat.Content of vanadium is the most inoperative, can produce embrittlement too much
Tendency.Considering, content of vanadium controls between 0.25%～0.35%.
Oxygen: high-strength temperature-resistant cold-forging steel, it is desirable to possess good delayed fracture resistance and fatigue behaviour, B, D class need to be mingled with into
Row is strict to be controlled, and B, D class is mingled with and has a strong impact on serviceability, i.e. oxide and brittle inclusion should give control, and [O] is at steel
Middle existence form mostly is compound form, and the total amount of field trash is directly proportional to oxygen content, so oxygen content is to evaluate field trash
Importance, therefore [O]≤15ppm is the content that the present invention is suitable.
Nitrogen: can expand and stable austenite, thus improve the elevated temperature strength of heat resisting steel.In steel containing chromium, manganese more time, can show
Write the dissolubility improving nitrogen, and available nitrogen alloying is to replace expensive nickel, but nitrogen content is too high easily causes processing
Hardening ratio is bigger than normal.In the present invention≤45ppm nitrogen content can play corresponding effect.
The technological design principle of the inventive method is: the present invention need to obtain good bainite structure, therefore, the most quickly
Being cooled to bainite transformation district, slow cooling is incubated, and promotes bainite transformation；It addition, use micro-zerolling on fast mill, reach
Purpose to crystal grain thinning；Crystal grain thinning is currently the only a kind of not only to improve the strength of materials but also increase the method for toughness.Steel tough
Crisp transition temperature and ferrite grain size d-1/2Linear.Crystal grain thinning improves the mechanism of toughness of material: crystal boundary is to split
The resistance of stricture of vagina extension, when crystal grain diminishes, grain boundary area increases, thus the dislocation number that forward position, interface plug amasss tails off, and is conducive to subtracting
Slow stress is concentrated, and the impurity concentration on crystal boundary face also diminishes simultaneously, and intergranular brittle fracture decreases.
Under relatively low heating-up temperature, reduce original austenite grains, it is to avoid mixed crystal, it addition, enter final rolling temperature and cold low
But, under initial temperature, control material in austenite Unhydrated cement finish rolling, disperse educt, crystal grain thinning, with ensure 7 grades and more than
Grain size control.
Use and have the beneficial effects that produced by technique scheme: the present invention uses Cr-V-Mo microalloying, it is ensured that unit
Uniformly, Control of gas content is excellent, makes wire rod have good heat resistance in element diffusion；The present invention possesses good intensity and heat is strong
Property, and not adding precious metal, cost is relatively low.
Heat-resistant stable is wanted by the inventive method by turbine high-strength bolt for downstream turbine making industry
Ask, by using converter → LF stove → RH stove → conticaster production technology, Cr-V-Mo microalloying, it is ensured that Elements Diffusion is uniform,
Control of gas content is excellent, makes wire rod have good heat resistance, it addition, adjust rolling line controlled rolling and controlled cooling production technology to realize former material
The crystal grain refinement of material, and control tissue predominantly bainite, grain size reach 7 grades and more than.Use conservative control rolling, cold
But technique realizes high strength heat resistant the cold heading steel and the production method thereof with good heat-resistant stable.The inventive method obtains
Wire rod, metallographic structure is mainly made up of bainite, grain size reach 7 grades and more than；By quenching+high tempering heat treatment
After, obtaining the heat-resistant stable of high-quality, heat resistance meets the creep-resistant property under 600 DEG C of high-temperature services.
The inventive method, without increasing equipment and investment, does not increase production cost, makes full use of existing equipment and technique, root
According to the requirement of the heat-resistant stable of downstream manufacturing enterprise, the high-strength bolt that gained wire rod is made is under 600 DEG C of conditions of high temperature
It is on active service, it is possible to keep good intensity and toughness index, there is good heat-resistant stable, intensity and heat resistance.
Accompanying drawing explanation
The present invention is further detailed explanation with detailed description of the invention below in conjunction with the accompanying drawings.
Fig. 1 is the metallograph of the embodiment of the present invention 1 gained wire rod；
Fig. 2 is the metallograph of the embodiment of the present invention 4 gained wire rod.
Detailed description of the invention
Composition proportion and the production method of this high strength heat resistant the cold heading steel are as described below:
Described wire rod composition is by weight percentage: C 0.38%～0.50%, Si 0.30%～0.40%, Mn 0.75%～
1.00%, P≤0.015%, S≤0.015%, Cr 0.90%～1.20%, Mo 0.35%～0.45%, V 0.25%～0.35%, [O]
≤ 15ppm, [N]≤45ppm, surplus is Fe and trace impurity.Specification limit is Φ 5.5～38mm.
Production method: (1) steel making working procedure: use converter smelting, before controlling argon, temperature is in the range of 1570～1590 DEG C；LF
Stove external refining, temperature of arriving at a station controls at 1490～1510 DEG C；RH stove vacuum outgas, inlet temperature controls at 1680～1700 DEG C
In the range of；Bloom continuous casting, casting speed control is 0.6～0.9m/min.
(2) cogging operation: continuous casting billet is heated to 1150～1250 DEG C, use 8 passage square passes be rolling to 160 ×
160mm square billet (steel billet).
(3) rolling process: include roughing, finish rolling and silking process；Heating steel billet is to 1150～1200 DEG C, after heating steel billet
Carrying out dephosphorization, the steel billet after de-scaling carries out 28 passes, 6 framves subtract sizing, finish rolling is weaved silk after terminating, laying temperature control
System is at 750～850 DEG C.
(4) refrigerating work procedure: enter Stelmor cooling line, regulation air-cooled line thermal insulation cover is opened quantity and blower fan aperture, is opened
Front two frame blower fans and front four thermal insulation covers, control cooldown rate at 1.5～2.0 DEG C/s；When being cooled to 580～620 DEG C, preferably
600 DEG C, thermal insulation cover covers entirely, and the cooling rate after control is at 0.5 DEG C/s and following.
The metallographic structure of wire rod that said method obtains is mainly bainite structure, grain size reach 7 grades and more than.
Embodiment 1: this high strength heat resistant the cold heading steel uses following technique to produce.
(1) steel-making and cogging operation: use converter smelting, before controlling argon, temperature is at 1570 DEG C；LF stove external refining, arrives at a station
Temperature controls at 1490 DEG C；RH stove vacuum outgas, inlet temperature controls at 1680 DEG C；Bloom continuous casting, casting speed control is at pulling rate
By 0.6m/min；The composition of gained continuous casting billet is by weight percentage: C 0.38%, Si 0.35%, Mn 0.85%, P 0.010%,
S 0.002%, Cr 0.94%, Mo 0.40%, V 0.31%, [O] 8ppm, [N] 30ppm, remaining is ferrum and trace impurity.
(2) cogging operation: continuous casting billet is heated to 1150 DEG C, is then rolled into steel billet.
(3) rolling and refrigerating work procedure: heating steel billet to 1150 DEG C；Laying temperature controls at 750 DEG C；Control leading portion cooling rate to exist
2.0 DEG C/s, control cooling rate after being cooled to 600 DEG C at 0.4 DEG C/s.
The present embodiment gained wire rod carries out grain size test, and test result is shown in Table 1；Carry out mechanical performance and high-temperature behavior is surveyed
Examination, test result is shown in Table 2.As it is shown in figure 1, as seen from the figure, its metallographic structure is predominantly for the metallograph of the present embodiment gained wire rod
Bainite structure.
Embodiment 2: this high strength heat resistant the cold heading steel uses following technique to produce.
(1) steel-making and cogging operation: use converter smelting, before controlling argon, temperature is at 1580 DEG C；LF stove external refining, arrives at a station
Temperature controls at 1500 DEG C；RH stove vacuum outgas, inlet temperature controls at 1690 DEG C；Bloom continuous casting, casting speed control is at pulling rate
By 0.7m/min；The composition of gained continuous casting billet is by weight percentage: C 0.48%, Si 0.40%, Mn 0.75%, P 0.010%,
S 0.010%, Cr 0.97%, Mo 0.39%, V 0.30%, [O] 9ppm, [N] 35ppm, remaining is ferrum and trace impurity.
(2) cogging operation: continuous casting billet is heated to 1200 DEG C, is then rolled into steel billet.
(3) rolling and refrigerating work procedure: heating steel billet to 1170 DEG C；Laying temperature controls at 780 DEG C；Control leading portion cooling rate to exist
1.7 DEG C/s, control cooling rate after being cooled to 600 DEG C at 0.5 DEG C/s.
The present embodiment gained wire rod carries out grain size test, and test result is shown in Table 1；Carry out mechanical performance and high-temperature behavior is surveyed
Examination, test result is shown in Table 2.
Embodiment 3: this high strength heat resistant the cold heading steel uses following technique to produce.
(1) steel-making and cogging operation: use converter smelting, before controlling argon, temperature is at 1590 DEG C；LF stove external refining, arrives at a station
Temperature controls at 1510 DEG C；RH stove vacuum outgas, inlet temperature controls at 1700 DEG C；Bloom continuous casting, casting speed control is at pulling rate
By 0.9m/min；The composition of gained continuous casting billet is by weight percentage: C 0.40%, Si 0.38%, Mn 0.85%, P 0.012%,
S 0.005%, Cr 1.20%, Mo 0.45%, V 0.28%, [O] 10ppm, [N] 45ppm, remaining is ferrum and trace impurity.
(2) cogging operation: continuous casting billet is heated to 1230 DEG C, is then rolled into steel billet.
(3) rolling and refrigerating work procedure: heating steel billet to 1200 DEG C；Laying temperature controls at 790 DEG C；Control leading portion cooling rate to exist
1.6 DEG C/s, control cooling rate after being cooled to 600 DEG C at 0.3 DEG C/s.
The present embodiment gained wire rod carries out grain size test, and test result is shown in Table 1；Carry out mechanical performance and high-temperature behavior is surveyed
Examination, test result is shown in Table 2.
Embodiment 4: this high strength heat resistant the cold heading steel uses following technique to produce.
(1) steel-making and cogging operation: use converter smelting, before controlling argon, temperature is at 1585 DEG C；LF stove external refining, arrives at a station
Temperature controls at 1505 DEG C；RH stove vacuum outgas, inlet temperature controls at 1690 DEG C；Bloom continuous casting, casting speed control is at pulling rate
By 0.8m/min；The composition of gained continuous casting billet is by weight percentage: C 0.45%, Si 0.36%, Mn 1.00%, P 0.011%,
S 0.007%, Cr 1.10%, Mo 0.42%, V 0.35%, [O] 12ppm, [N] 40ppm, remaining is ferrum and trace impurity.
(2) cogging operation: continuous casting billet is heated to 1220 DEG C, is then rolled into steel billet.
(3) rolling and refrigerating work procedure: heating steel billet to 1150 DEG C；Laying temperature controls at 800 DEG C；Control leading portion cooling rate to exist
1.5 DEG C/s, control cooling rate after being cooled to 600 DEG C at 0.5 DEG C/s.
The present embodiment gained wire rod carries out grain size test, and test result is shown in Table 1；Carry out mechanical performance and high-temperature behavior is surveyed
Examination, test result is shown in Table 2.As in figure 2 it is shown, as seen from the figure, its metallographic structure is predominantly for the metallograph of the present embodiment gained wire rod
Bainite structure.
Embodiment 5: this high strength heat resistant the cold heading steel uses following technique to produce.
(1) steel-making and cogging operation: use converter smelting, before controlling argon, temperature is at 1575 DEG C；LF stove external refining, arrives at a station
Temperature controls at 1495 DEG C；RH stove vacuum outgas, inlet temperature controls at 1685 DEG C；Bloom continuous casting, casting speed control is at pulling rate
By 0.85m/min；The composition of gained continuous casting billet is by weight percentage: C 0.50%, Si 0.32%, Mn 0.94%, P
0.015%, S 0.012%, Cr 0.90%, Mo 0.37%, V 0.25%, [O] 11ppm, [N] 38ppm, remaining is ferrum and trace
Impurity.
(2) cogging operation: continuous casting billet is heated to 1250 DEG C, is then rolled into steel billet.
(3) rolling and refrigerating work procedure: heating steel billet to 1180 DEG C；Laying temperature controls at 820 DEG C；Control leading portion cooling rate to exist
1.9 DEG C/s, control cooling rate after being cooled to 580 DEG C at 0.2 DEG C/s.
The present embodiment gained wire rod carries out grain size test, and test result is shown in Table 1；Carry out mechanical performance and high-temperature behavior is surveyed
Examination, test result is shown in Table 2.
Embodiment 6: this high strength heat resistant the cold heading steel uses following technique to produce.
(1) steel-making and cogging operation: use converter smelting, before controlling argon, temperature is at 1580 DEG C；LF stove external refining, arrives at a station
Temperature controls at 1500 DEG C；RH stove vacuum outgas, inlet temperature controls at 1695 DEG C；Bloom continuous casting, casting speed control is at pulling rate
By 0.75m/min；The composition of gained continuous casting billet is by weight percentage: C 0.44%, Si 0.30%, Mn 0.89%, P
0.010%, S 0.015%, Cr 1.06%, Mo 0.35%, V 0.33%, [O] 15ppm, [N] 36ppm, remaining is ferrum and trace
Impurity.
(2) cogging operation: continuous casting billet is heated to 1180 DEG C, is then rolled into steel billet.
(3) rolling and refrigerating work procedure: heating steel billet to 1190 DEG C；Laying temperature controls at 850 DEG C；Control leading portion cooling rate to exist
1.8 DEG C/s, control cooling rate after being cooled to 620 DEG C at 0.4 DEG C/s.
The present embodiment gained wire rod carries out grain size test, and test result is shown in Table 1；Carry out mechanical performance and high-temperature behavior is surveyed
Examination, test result is shown in Table 2.
Grain size is tested: first corrode under mass fraction 4% nitric acid ethanol, uses metallography microscope Microscopic observation gold
Phase constitution, metallographic structure is a small amount of ferrite+a large amount of bainite structures.After using Φ 16mm wire rod to quench, use and use
The picric acid ethanol solution of mass fraction 5% is heated to 70 DEG C and carries out etch, then tissues observed crystal grain under metallurgical microscope
Degree, checks numerical value such as table 1；Grain size all controls for 8～9.5 grades.
Table 1: the grain size test result of embodiment 1-6
Mechanical performance and high-temperature behavior test: first use GB/T 228 method to carry out tension test, at universal tensile wire rod
Carry out on testing machine, tensile strength, elongation after fracture are measured；It is sudden and violent that high-temperature stability and heat resistance index are respectively adopted heat
Dew and high-temperature creep resistance are evaluated, and embodiment gained wire rod is carried out heat treatment, and heat treatment post-treatment becomes the mark of Φ 5mm
Quasi-stretching and creep sample, carry out thermally-stabilised and creep test respectively, and heat stabilization test technique is 600 DEG C/100h, after beat exposure
Room temperature tensile again；Creep test technique is 600 DEG C/250MPa/100h, at RD2Carrying out on type testing machine, inspection numerical value is shown in Table 2.
Table 2: the mechanical performance of embodiment 1-6 and high-temperature behavior test result
| Sample | Embodiment 1 | Embodiment 2 | Embodiment 3 | Embodiment 4 | Embodiment 5 | Embodiment 6 |
| Specification | Φ5.5mm | Φ16mm | Φ38mm | Φ24mm | Φ14mm | Φ30mm |
| Tensile strength | 1150MPa | 1220 MPa | 1120 MPa | 1140 MPa | 1250 MPa | 1100 MPa |
| Section elongation percentage | 21.5% | 20.0% | 24.5% | 23.0% | 19.5% | 22.0% |
| Tensile strength after 600 DEG C/100h beat exposure | 1025MPa | 1035MPa | 1053MPa | 1060MPa | 1045MPa | 1020MPa |
| 600 DEG C/250MPa/100h high temperature creep property (ε/%) | 0.047 | 0.053 | 0.090 | 0.101 | 0.049 | 0.072 |
Claims (9)
1. a high strength heat resistant the cold heading steel, it is characterised in that its composition is by weight percentage: C 0.38%～
0.50%, Si 0.30%～0.40%, Mn 0.75%～1.00%, P≤0.015%, S≤0.015%, Cr 0.90%～1.20%, Mo
0.35%～0.45%, V 0.25%～0.35%, [O]≤15ppm, [N]≤45ppm, surplus is Fe and trace impurity.
High strength heat resistant the cold heading steel the most according to claim 1, it is characterised in that: the metallographic structure master of described wire rod
To be made up of bainite.
High strength heat resistant the cold heading steel the most according to claim 1 and 2, it is characterised in that: described wire rod specification is Φ
5.5～38mm.
4. the production method of a high strength heat resistant the cold heading steel, it is characterised in that: it includes steel-making, cogging, rolling and cold
But operation；Described steel making working procedure includes converter smelting, LF stove refine, RH stove vacuum outgas and casting process, and gained continuous casting billet becomes
The percentage by weight divided: C 0.38%～0.50%, Si 0.30%～0.40%, Mn 0.75%～1.00%, P≤0.015%, S≤
0.015%, Cr 0.90%～1.20%, Mo 0.35%～0.45%, V 0.25%～0.35%, [O]≤15ppm, [N]≤45ppm,
Surplus is Fe and trace impurity.
The production method of high strength heat resistant the cold heading steel the most according to claim 4, it is characterised in that described steelmaker
Sequence: the inlet temperature of LF stove refine is 1490～1510 DEG C；The inlet temperature of RH stove vacuum outgas is 1680～1700 DEG C.
The production method of high strength heat resistant the cold heading steel the most according to claim 4, it is characterised in that described steelmaker
Sequence: the pulling rate of casting process is 0.6～0.9m/min.
The production method of high strength heat resistant the cold heading steel the most according to claim 4, it is characterised in that described cogging work
Sequence: continuous casting billet is heated to 1150～1250 DEG C and carries out cogging.
The production method of high strength heat resistant the cold heading steel the most according to claim 4, it is characterised in that described rolling work
Sequence: be heated to 1150～1200 DEG C and roll, laying temperature is at 750～850 DEG C.
9., according to the production method of the high strength heat resistant the cold heading steel described in claim 4-8 any one, its feature exists
In: described refrigerating work procedure: control cooldown rate, at 1.5～2.0 DEG C/s, controls cooldown rate and exists after being cooled to 580～620 DEG C
0.5 DEG C/s and following.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107881423A (en) * | 2017-12-27 | 2018-04-06 | 南京宝日钢丝制品有限公司 | The method of cold-forging steel and preparation method with preparing steel wire using the cold-forging steel |
| CN109023103A (en) * | 2018-09-25 | 2018-12-18 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of bainite cold heading steel wire rod |
| CN110358965A (en) * | 2019-07-02 | 2019-10-22 | 江阴兴澄合金材料有限公司 | 100 grades a kind of or more high-test chain wire rod and its manufacturing method |
| CN110724807A (en) * | 2019-09-23 | 2020-01-24 | 邢台钢铁有限责任公司 | Low-alloy high-strength heat-resistant steel wire rod with good cold forming performance and preparation method thereof |
| CN113198989A (en) * | 2021-03-31 | 2021-08-03 | 邯郸钢铁集团有限责任公司 | Method for improving reduction of area of chromium-molybdenum steel high-strength bolt for automobile |
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Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101098979A (en) * | 2005-02-16 | 2008-01-02 | 新日本制铁株式会社 | Hot rolled wire material excellent in cold forging property after spheroidizing treatment, spheroidizing-annealed steel wire having excellent cold forging property, and method for production thereof |
| CN102676929A (en) * | 2012-06-01 | 2012-09-19 | 南京钢铁股份有限公司 | Method for manufacturing spheroidizing-free high-quality high-strength cold forging steel |
| CN103952633A (en) * | 2014-04-30 | 2014-07-30 | 邢台钢铁有限责任公司 | high-strength steel wire rod with good low temperature impact toughness and production method thereof |
-
2016
- 2016-08-04 CN CN201610632572.0A patent/CN106086652A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101098979A (en) * | 2005-02-16 | 2008-01-02 | 新日本制铁株式会社 | Hot rolled wire material excellent in cold forging property after spheroidizing treatment, spheroidizing-annealed steel wire having excellent cold forging property, and method for production thereof |
| CN102676929A (en) * | 2012-06-01 | 2012-09-19 | 南京钢铁股份有限公司 | Method for manufacturing spheroidizing-free high-quality high-strength cold forging steel |
| CN103952633A (en) * | 2014-04-30 | 2014-07-30 | 邢台钢铁有限责任公司 | high-strength steel wire rod with good low temperature impact toughness and production method thereof |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107881423A (en) * | 2017-12-27 | 2018-04-06 | 南京宝日钢丝制品有限公司 | The method of cold-forging steel and preparation method with preparing steel wire using the cold-forging steel |
| CN109023103A (en) * | 2018-09-25 | 2018-12-18 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of bainite cold heading steel wire rod |
| CN110358965A (en) * | 2019-07-02 | 2019-10-22 | 江阴兴澄合金材料有限公司 | 100 grades a kind of or more high-test chain wire rod and its manufacturing method |
| CN110358965B (en) * | 2019-07-02 | 2021-04-09 | 江阴兴澄合金材料有限公司 | Wire rod for 100-grade or above high-strength chain and manufacturing method thereof |
| CN110724807A (en) * | 2019-09-23 | 2020-01-24 | 邢台钢铁有限责任公司 | Low-alloy high-strength heat-resistant steel wire rod with good cold forming performance and preparation method thereof |
| CN110724807B (en) * | 2019-09-23 | 2021-04-02 | 邢台钢铁有限责任公司 | Low-alloy high-strength heat-resistant steel wire rod with good cold forming performance and preparation method thereof |
| EP4060072A4 (en) * | 2019-12-18 | 2024-06-12 | Posco | Wire rod and component, for cold forging, each having excellent delayed fracture resistance characteristics, and manufacturing methods therefor |
| CN113198989A (en) * | 2021-03-31 | 2021-08-03 | 邯郸钢铁集团有限责任公司 | Method for improving reduction of area of chromium-molybdenum steel high-strength bolt for automobile |
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Application publication date: 20161109 |